Method of making an optical fiber with an axially decreasing group velocity dispersion

ABSTRACT

An optical fiber preform is made by supplying the base glass reactant and the dopant glass reactant to a burner that generates a flame in which a stream of glass particles is produced. The burner moves with respect to a rotating mandrel to deposit layers of glass particles on the mandrel. During the deposition of a portion of the preform, the flow rate of the dopant glass reactant is varied in accordance with a first recipe of dopant flow as a function of burner position as the burner moves longitudinally along the substrate to form one of the layers. The flow rate of the dopant glass reactant varies in accordance with a second recipe of dopant flow as a function of burner position as the burner moves longitudinally along the substrate to form a layer adjacent to the one layer. The second recipe is different from the first recipe, and the flow rate of the dopant glass reactant changes during the step of moving the reaction zone to form the one layer.

CROSS-REFERENCE TO RELATED APPLICATION

This is a continuation-in-part of U.S. patent application Ser. No. 08/477,679, abandon filed Jun. 7, 1995, which is a division of U.S. patent application Ser. No. 08/172,937, filed Dec. 27, 1993 now U.S. Pat. No. 5,504,829.

BACKGROUND OF THE INVENTION

The present invention relates to methods of making preforms from which optical fibers can be drawn; these methods are especially useful for making high data rate optical fibers for telecommunication systems.

It has been known that solitons can be generated in optical fibers when the transmission power is in the nonlinear region. The optical soliton maintains its narrow temporal pulse as it propagates down the fiber because the dispersion is balanced with the nonlinear index. Mathematically this phenomenon is adequately described with the well known nonlinear Schroedinger equation. See, for example, the publication, C. Sien, "Concatenated Soliton Fibre Link", Electronics Letters, volume 12, pages 237-238 (1991). There are three important terms in the nonlinear Schroedinger equation. These terms relate to attenuation, the group velocity dispersion and the nonlinear index effects. The balancing of the group velocity dispersion with the nonlinear index term has received much attention to date and is well known. However, pulses propagating in real fibers undergo attenuation; this can cause soliton pulses to develop frequency chirping and subsequent broadening and to then become essentially linear.

As used herein the term "dispersion" means group velocity dispersion, which is the total of the material dispersion and the refractive index profile dispersion.

It has been proposed that a soliton can survive in a fiber with loss if the group velocity dispersion can be made to decrease approximately exponentially with distance (K. Tajima, "Compensation of Soliton Broadening in Nonlinear Optical Fibers with Loss", Optics Letters, volume 12(1), pp. 54-56, 1987). In this way, the group velocity dispersion is made to continuously change so that it matches the changing power level. That publication states that this can be accomplished by varying the core diameter through fiber tapering and that such a fiber can be manufactured by controlling the fiber draw speed. Such a fiber is illustrated in FIG. 1 wherein the diameter of fiber 5 exponentially decreases from the large diameter input end 6 to the small diameter output end 7. The diameter of the core of fiber 5 is proportional to the outside diameter of the fiber. In the theoretical example proposed by Tajima the effective core diameter of such a fiber changes exponentially from about 10 μm to about 5 μm over 100 km.

A dispersion decreasing fiber was actually made by varying the speed of the fiber draw to change the fiber outer diameter from 175 μm to 115 μm, whereby the measured dispersion decreased from 10 ps/nm-km to 1 ps/nm-km over a 1 km length (V. A. Bogatyrev et al., "A single-mode fiber with chromatic dispersion varying along the length", Journal of Lightwave Technology, volume 9(5), pages 561-566, 1991). Subsequently, that fiber was used to generate a continuous soliton pulse train at 70 Gb/s (S.V. Chernikov, "70 Gbit/s fibre based source of fundamental solitons at 1550 nm", Electronics Letters, volume 28(13), pages 1210-1211, 1992). Such fibers have potential application in ultrahigh bit rate telecommunication systems of the type schematically illustrated in the soliton communication system of FIG. 2. A pulse train is input to amplifier 11 and coupled to dispersion decreasing fiber DDF-15, the dispersion at the input end a being greater than that at output end b. After propagating a distance that is limited by the maximum dispersion change, the optical signal is again amplified at amplifier 12 and coupled to dispersion decreasing fiber DDF-16, which has a high dispersion end a adjacent amplifier 12 and a low dispersion end b adjacent amplifier 13.

It has also been suggested that dispersion-decreasing fiber may be useful in a soliton communication line to extend the distance between amplifiers 11 and 12, for example. While there clearly could be numerous applications of dispersion-decreasing fiber, a tapered fiber, in which the outside diameter as well as the core diameter changes to the extent proposed in the Tajima and Bogatyrev et al. publications, will result in problems with splicing and cabling, for example.

SUMMARY OF THE INVENTION

It is therefore an object of the present invention to provide a method of making a constant diameter optical fiber, the dispersion of which varies along the length thereof. Another object is to provide a method of making a dispersion decreasing optical fiber in which an axial change in dispersion is not totally dependent upon a change in the outside diameter of the fiber. Yet another object is to provide a method of making an optical fiber in which the refractive index profile varies along the length thereof.

Briefly, the present invention relates to a method of making optical fibers such as dispersion decreasing fibers. In accordance with one embodiment, a core preform is formed by flowing a base glass reactant and a dopant glass reactant to a reaction zone adjacent to an elongated substrate and moving the reaction zone from one end of the substrate to the other to form a layer. The deposition of layers is continued to form a preform. During the deposition of a portion of the preform, the flow rate of the dopant glass reactant is varied in accordance with a first recipe of dopant reactant flow as a function of reaction zone position as the reaction zone moves longitudinally along the substrate to form one of the layers. The flow rate of the dopant glass reactant varies in accordance with a second recipe as the reaction zone moves longitudinally along the substrate to form a layer adjacent to the one layer. The second recipe is different from the first recipe, and the flow rate of the dopant glass reactant changes during the step of moving the reaction zone to form the one layer.

In another embodiment, an optical fiber core preform is formed by depositing on an elongated mandrel a plurality of coatings, each coating being formed of a plurality of layers of glass particles, each coating having a unique refractive index profile. The mandrel is removed to form a porous preform, and the porous preform is heated to form a dense glass preform. The improvement comprises depositing one of the coatings such that its thickness is nonuniform, the thickness of the one coating being greater at one end of the preform than at the opposite end of the preform.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic illustration of a prior art optical fiber for soliton propagation.

FIG. 2 schematically depicts a soliton communication system employing dispersion decreasing optical fibers.

FIG. 3 is a refractive index profile of the core of a dispersion shifted single-mode optical fiber.

FIGS. 4(a) to 4(j) and FIGS. 5(a) to 5(d) are refractive index profiles of cores at the input and/or output ends of single-mode optical fibers made in accordance with the invention.

FIGS. 6 and 8 are refractive index profiles of two types of optical fibers having flat-topped central core regions.

FIGS. 7 and 9 are graphs in which both dispersion and mode field diameter are plotted as a function of flat top length x for the profiles of FIGS. 6 and 8, respectively.

FIG. 10 is a schematic illustration of an apparatus that can be employed to form the optical fibers of the present invention.

FIG. 11 is a cross-sectional view of a porous core preform formed by a modified process.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

In potential applications of dispersion-decreasing fiber, it is desirable to achieve a large variation in dispersion between the input and output ends of the fiber. Additionally, for soliton transmission, the dispersion must remain positive and become very small or reach zero by the output end of the fiber. Other fiber characteristics that must be considered are mode field diameter and cutoff wavelength, since refractive index modifications that affect dispersion can also affect these characteristics.

Since solitons require low loss operation, it is preferable to operate in the 1550 nm region of the electromagnetic spectrum where silica based optical fibers exhibit extremely low loss. Dispersion-shifted fiber made in accordance with the teachings of U.S. Pat. No. 4,715,679 can be designed for zero dispersion at about 1550 nm. Dispersion-shifted fiber is further discussed in the publications: T. D. Croft et al. "Low-Loss Dispersion-Shifted Single-Mode Fiber Manufactured by th OVD Process", Journal of Lightwave Technology, Volume LT-3, No. 5, October 1985, pp. 9313-934; and V. A. Bhagavatula et al. "Bend-Optimized Dispersion-Shifted Single-Mode Designs", Journal of Lightwave Technology, Volume LT-3, No. 5, October 1985, pp. 954-957.

FIG. 3 illustrates the refractive index profile of a typical, commercially available dispersion shifted fiber exhibiting zero dispersion at 1550 nm. The fiber core comprises a central core region 20 that is separated from an outer ring 21 by a region 22 of depressed refractive index. The diameter of its central triangular region 20 is 7.20 μm. and the inner and outer diameters of ring 21 are 10.08 μm and 12.94 μm. respectively. The peak refractive index values of regions 20 and 21 (expressed as Δ_(P)) are 0.9% and 0.3%, respectively. The term Δ_(P) is the relative refractive index of the core with respect to that of the cladding and is given by

    Δ.sub.P =(n.sub.1.sup.2 -n.sub.2.sup.2)/2n.sub.1.sup.2

where n₁ is the peak refractive index of the core region and n₂ is the refractive index of the cladding. For simplicity of expression, Δ is often expressed in percent, i.e. one hundred times Δ. It is noted that some processes for producing optical fibers result in a refractive index depression at the fiber centerline. In such a fiber, n₁ refers to the maximum refractive index of the central core region.

In accordance with one aspect of the invention, the refractive index profile of a dispersion decreasing optical fiber is a variation of the dispersion shifted profile of FIG. 3 throughout its length, the profile constantly changing along the fiber length to provide the required change from a relatively large dispersion at the input end to a relatively low or zero dispersion at the output end. In a preferred embodiment, the profile at the output end of the fiber is the dispersion-shifted profile that produces essentially zero dispersion at the operating wavelength. Some of these profiles offer the advantage of achieving large dispersion change with minimal refractive index profile variation. However, a design tradeoff exists between the complexity of the modified profile and the range of possible values of the group velocity dispersion. Designs for varying the cross-sectional refractive index profile as a function of length can be conveniently divided into three types:

Type I--those that leave the central core region of the nominal dispersion-shifted fiber of FIG. 3 unchanged, only the outer ring structure being modified;

Type II--those that modify only the central core region; and

Type III--those that modify both the central region and the ring region.

The Type I group of profiles requires fewer changes in the glass particle deposition step of the fiber core fabrication process, since the central core region remains unchanged throughout the length of the fiber. However, they also have a smaller range of potential dispersion change. Two further constraints limiting possible profiles are that the fiber must remain single mode and dispersion must remain positive.

Table 1 lists parameters associated with the refractive index profiles of FIGS. 3, 4(a) through 4(j) and FIG. 5(a) through 5(d). The values of dispersion, mode-field diameter and cut-off wavelength listed in Table 1 FIG. 5(a) through 5(d). The values of dispersion, mode-field diameter and cut-off wavelength listed in Table 1 have been derived by computer simulation techniques.

                  TABLE 1     ______________________________________              Dispersion  Mode Field                                    Cutoff              (ps/nm/km)  Diameter  Wavelength, λ.sub.c     Profile  at 1550 nm  (pm)      (nm)     ______________________________________     FIG. 3   0.0         8.7       1106     FIG. 4(a)              1.978       10.1      1524     FIG. 4(b)              1.485       9.9       1480     FIG. 4(c)              0.919       9.5        936     FIG. 4(d)              0.599       9.5       1372     FIG. 4(e)              7.267       10.3      1526     FIG. 4(f)              7.794       10.0      1385     FIG. 4(g)              2.969       9.2       1089     FIG. 4(h)              7.267       10.3      1526     FIG. 4(i)              6.386       9.3       1277     FIG. 4(j)              5.794       9.7       1393     FIG. 5(a)              3.513       6.4       1276     FIG. 5(b)              14.396      6.8       1552     FIG. 5(c)              2.940       8.4       1193     FIG. 5(d)              8.902       8.3       1447     ______________________________________

Type I profiles are illustrated in FIGS. 3 and 4(a) through 4(j); these profiles differ in that the rings of the outer core region have different doping concentrations and shapes, the ring completely disappearing in FIG. 4(c). The characteristics for these types of profiles are summarized in Table 1. The optical characteristics of fibers represented by FIGS. 4(a) through 4(j) are such that any of those fibers could be employed at the high dispersion input end of a dispersion decreasing fiber, provided that a profile of lower dispersion exists at the opposite end. For example, any of the profiles represented by FIGS. 4(a) through 4(j) could be employed at the high dispersion input end of the fiber if the profile represented by FIG. 3 were employed at the low dispersion output end. In another example, the profile represented by FIG. 4(i) could be employed at the high dispersion end of the fiber and the profile represented by FIG. 4(g) could be employed at the low dispersion end. Fibers having the profiles of FIGS. 4(a) through 4(d) and 4(g) exhibit dispersions less than 3 ps/nm/km. Thus, such fibers would not produce enough dispersion change to make them useful in systems with large discrete amplifier spacing unless the core was also provided with taper, such as by varying the speed of the fiber draw operation.

Table 1 reveals that the largest dispersion occurs in profiles where there is a sharp edge in the refractive index profile near the core center (see FIGS. 4(e), 4(f) and 4(i), for example). However, practical considerations such as germanium oxide diffusion may limit the sharpness of profile edges. For this reason, of the family of profiles that includes the profiles of FIGS. 4(e) through 4(j), the profile of FIGS. 4(g) and 4(h) may be easier to fabricate.

Table 1 also reveals that dispersion increases as the diameter of the central core region increases; compare the dispersions of the profiles of FIGS. 5(c) and 5(d) with the zero dispersion produced by the profile of FIG. 3.

The Table 1 entries for FIGS. 5(a) and 5(b) illustrate that large dispersion at reasonable mode field diameter can be achieved by making the central core region flat-topped. A comparison between FIGS. 5(a) and 5(b) shows that dispersion is highly sensitive to the location of the outer radius of the central core portion. It would also be sensitive to its slope. Furthermore, changes in the ring profile could be used to tailor the mode field diameter or cut-off wavelength.

Further examples of flat-topped refractive index profiles are illustrated in FIGS. 6 and 8, the dispersion and mode field diameters of those profiles being illustrated in FIGS. 7 and 9, respectively. When x equals zero, the profiles of FIGS. 6 and 8 are optimized for zero dispersion in the 1550 nm range. The following discussion shows that large positive dispersion can be introduced by inserting the flat-topped central region. The addition of such a flat-topped central region to any optimized zero dispersion profile can introduce large positive dispersion.

In the refractive index profile of FIG. 6 the central core region comprises a flat-topped portion 47 and a region 48, the refractive index of which decreases with radius. The radius of region 47 is x μm. Spaced from the central core region is annular outer core region 49. If x equalled zero, the profile would be the same as that of FIG. 3. If the radius of portion 47 were x μm, then the inner radius of region 49 would be (x+5) μm.

FIG. 7 is a graph in which both dispersion and mode field diameter are plotted as a function of flat top length x. Curves 50 and 51 respectively show that dispersion increases and mode filed diameter decreases with an increase in flat top length x.

In the refractive index profile of FIG. 8 the central core region comprises a flat-topped central core region 53 of given refractive index surrounded by outer core region 55 of refractive index lower than the given refractive index. This type of refractive index profile is similar to that taught in U.S. Pat. No. 4,755,022 (Ohashi et al) which is incorporated herein by reference. Whereas regions 53 and 55 are illustrated as being step-type profiles, they could be graded as suggested by the Ohashi et al. patent.

Curve 57 of FIG. 9 shows that dispersion increases with an increase in flat top length x. Mode field diameter (curve 58) first decreases and then increases as x increases from zero to about 5 μm.

There is a common feature in the refractive index profiles of FIGS. 6 and 8. Each has a central core region and an outer core region of lower refractive index than the central region. The outer region acts as a high index mass which is located outside that core radius where the power increases with longer wavelength. The extent of the mass is determined by its refractive index profile, which includes its radius. The index profile can be designed such the power weighted integral of the mass of the outer core region balances that of the inner core region giving the desired dispersion value, which may be zero. An index depression such as depression 46 of FIG. 6 allows more flexibility in placing the outer mass where it will have desirable effects on the other fiber properties such as mode field diameter and cutoff wavelength.

Decreasing dispersion single-mode optical fibers can be made in accordance with FIG. 10 which schematically illustrates the outside vapor deposition (OVD) process wherein glass particles are deposited on the longitudinal surface of a mandrel. Other glass deposition processes could be employed to form dispersion decreasing fibers or at least portions thereof. Examples of such processes are the modified chemical deposition (MCVD) process whereby glass layers are deposited un the inner surface of a substrate tube and the axial vapor deposition (AVD) process.

Referring to FIG. 10, a mandrel 60 of silica or other high temperature material is rotated and translated along its longitudinal axis as shown by arrows 64a and 64b, respectively. Burner 65 produces a stream 66 of glass particles which deposits on mandrel 60, each pass or traverse of the burner along the mandrel depositing an adherent layer. Each of the coatings 68, 69, 70 and 71 is formed of a plurality of such layers. The speed of burner traverse can be varied. traverse of the burner along the mandrel depositing an adherent layer. Each of the coatings 68, 69, 70 and 71 is formed of a plurality of such layers. The speed of burner traverse can be varied.

Each coating is formed of glass particles comprising a base glass such as silica (SiO₂), and it optionally contains a dopant such as GeO₂, P₂ O₅, B₂ O₃ or the like for modifying the refractive index of the base glass. The dopants GeO₂ and P₂ O₅ increase the refractive index of silica, and B₂ O₃ lowers the refractive index when added to silica. To form particles of GeO₂ -doped silica, reactants such as SiCl₄ and GeCl₄ are supplied along with oxygen to burner 65. In the system of FIG. 10, vapors of SiCl₄ and GeCl₄ are formed in reservoirs 74 and 75, respectively. These vapors are metered by flow controllers 77 and 78, respectively, as taught in U.S. Pat. No. 4,314,837. Oxygen from source 76 is metered by flow controller 79. The amount of reactants flowing through controllers 77, 78 and 79 is controlled by system controller 80. Flow controllers having a response time of 0.5-1.5 seconds are manufactured by Tylan Corporation of Carson, Calif.

The flow of all reactants sometimes remains constant during the deposition of an entire layer of glass particles. Alternatively, the flow of one or more of the reactants can vary as a function of the longitudinal position of the burner. Dashed line 81 connecting burner 65 to system controller 80 shows that controller 80 is provided with a signal that indicates the position of the burner with respect to the longitudinal axis of the mandrel.

The concentration of each of the glass constituents as a function of burner position along the longitudinal axis of the mandrel during the formation of a single layer is referred to as a recipe. If burner traverse rate is constant, then a recipe for a single burner pass can be defined in terms of the reactant flow rates of all reactants as a function of burner position.

If two identical layers are to be deposited adjacent one another, the deposition of the first and second layers can be started at a first end of the mandrel, or deposition of the first layer can start at the first end of the mandrel, and deposition of the second layer can start at the second end. If the first and second layers are identical, both consisting of a base glass and a dopant glass, the concentration of which varies with position along the mandrel axis, then the first and second recipes are identical, regardless of whether the burner deposits the first and second layers starting from the same end of the mandrel or starting from different ends of the mandrel. The reason for this is that the recipe determines the composition of the deposited glass particles as a function of burner position along the mandrel axis and not as a function of time lapse after the commencement of the deposition of the layer.

Assume that it is desired to form an optical fiber having the refractive index profile of FIG. 4(g) at one end and that of FIG. 3 at the opposite end. If the entire fiber is to be 25 km long, for example, preform 72 can be deposited such that it can be drawn to a length of 25 km. In the profiles of FIGS. 4(g) and 3, the central core region has a diameter of 7.2 μm and a Δ_(P) of 0.9%. Also, in FIGS. 4(g) and 3, the radial width of the outer core region or ring is 1.43 μm. The only difference between the profiles of FIGS. 4(g) and 3 is the position of the outer core regions. In FIG. 4(g), those regions are immediately adjacent the central core region, and in FIG. 3 those regions are separated from the central core region by 1.44 μm in the resultant fiber.

One technique for forming such a fiber would be to first form coating 68 by depositing the first layer thereof such that it contains SiO₂ doped with a sufficient amount of GeO₂ to provide a Δ_(P) of 0.9%. In each of the subsequent layers that are deposited to form coating 68, the amount of GeCl₄ flowing to the burner is decreased until the last layer contains the smallest incremental amount of GeO₂ (corresponding to the fiber radius of 3.6 μm). With the flow of GeCl₄ turned off, a coating 69 of pure silica (SiO₂) is deposited in a thickness which varies from a predetermined thickness at end 62 of the preform to zero thickness at end 63. This can be accomplished by providing a predetermined flow of SiCl₄ at end 62 and decreasing the flow of SiCl₄ until it is completely cut off when the burner reaches end 63. Alternatively, the flow rate of SiCl₄ could remain constant and the burner speed could be varied.

Coating 70 is then formed by depositing a plurality of layers of glass particles, the first of which contains no GeO₂, ramping the flow of GeCl₄ so that the middle layer contains sufficient GeO₂ to provide a Δ_(P) of 0.3%, and thereafter decreasing the flow rate of GeCl₄ until the deposition of the outer layer which contains no GeO₂. An outer coating 71 of pure SiO₂ can then be deposited. Coating 71 could have a uniform thickness as shown in FIG. 10. Alternatively, it could be deposited such that its thickness at end 63 is greater than its thickness at end 62, whereby it counteracts the effect of coating 69 and causes the diameter of core preform 72 to be uniform throughout its length. Preform 72 is preferably consolidated prior to applying the remainder of the cladding glass particles thereto. This can be done by removing mandrel 60 from the porous preform and then heating the preform in a consolidation furnace to a temperature sufficiently high to consolidate the glass particles and form a dense glass core preform. Cladding material is then applied to the core preform. This can be done by inserting the core preform into chucks so that it can be rotated and translated with respect to burner 65 to deposit a cladding of undoped silica particles, for example. The resultant fiber preform is consolidated to form a draw blank from which optical fiber is drawn.

Rather than forming a blank from which one length of dispersion decreasing fiber can be drawn, a larger blank can be formed, and many such fibers can be drawn from it. The pattern of coatings shown in FIG. 10 would be repeated along the length of the preform. Thus, when the preform is drawn into fiber, the dispersion would decrease from a high value to a low value along one section of the drawn fiber having a length of 25 km, for example. Then the dispersion would abruptly increase to the high value and decrease along the next 25 km. This pattern of decreasing dispersion would be repeated for all of the fiber lengths drawn from the blank.

An alternative preform deposition embodiment is shown in FIG. 11 wherein elements similar to those of FIG. 10 are represented by primed reference numerals. The burner and reactant control system is not shown in FIG. 11 as those elements are the same as those shown in FIG. 10. Tapered coating 69 of FIG. 10 is not deposited. Rather, after central core coating 68' is deposited, the flow rate of GeCl₄ (and optionally the flow rate of SiCl₄) is gradually changed as the burner traverses from end 62' to end 63' of the preform. For this example, burner 66 begins each particle deposition pass at end 62', and it rapidly traverses from end 63' to end 62' without depositing particles. After the deposition of coating 68', the flow rate of GeCl₄ is zero and that of SiCl₄ is at a maximum. At this point in the process, the burner is positioned at end 62' where the profile of FIG. 3 is to be formed. During the first pass of the burner along the preform during the formation of the first layer of coating 85, the flow rate of GeCl₄ would therefor be zero at end 62', and GeCl₄ would begin to flow only at end 63'. During the second pass of the burner along the preform during the formation of the second layer of coating 85, the flow rate of GeCl₄ begins at some incremental distance from end 63', and it increases as the burner approaches end 63'. At that pass corresponding to the deposition of the middle of depressed index region 22 at end 62', the burner is supplied with sufficient GeCl₄ at end 63' to form glass particles having a Δ_(P) of 0.3%, corresponding to the peak index of the outer region of FIG. 4(g). At that point in the process when GeCl₄ is being fed to the burner to just begin to form the inner radius of index ring 21 (FIG. 3) at end 62', the GeCl₄ ceases flowing during the remainder of the pass. This kind of ramped flow of GeCl₄ to the burner continues until the last pass of the formation of coating 85, when no GeCl₄ flows since the outer portion of ring 21 (FIG. 3) contains no GeO₂, and the corresponding radius of the profile of FIG. 4(g) contains no GeO₂. A coating 71' of SiO₂ can then be deposited as described above. Preform 87 can then be consolidated, overclad with SiO₂, and drawn into optical fiber.

An optical fiber similar to that produced by the method discussed above in conjunction with FIG. 11 can be made by the MCVD process. A burner moves along the outside surface of a silica substrate tube from a first end to a second end to form within the tube a moving hot zone or reaction zone. The burner then rapidly returns to the first end. A base glass reactant and at least one dopant glass reactant are flowed into the first end of the tube. The reactants form glass particles in the reaction zone; these particles deposit downstream of the reaction zone on the inner surface of the tube. As the reaction zone moves from the first end to the second end, a first layer of particles is formed. The reaction zone returns to the first end and repeats its traverse of the tube to form a second layer. Additional layers are deposited over the first and second layer to form a coating. One or more coatings form a preform from which optical fiber can be drawn.

During the deposition of a portion of the preform, the flow rate of dopant glass reactant is varied in accordance with a given recipe as the reaction zone moves longitudinally along the substrate tube to form one of the layers. The flow rate of the dopant glass reactant varies in accordance with a recipe different from the given recipe as the reaction zone moves longitudinally along the substrate to form a layer adjacent to the one layer. The effect of this method is to form a preform having a refractive index profile having a first shape (such as that shown in FIG. 4(g)) at a first end, a refractive index profile having a second shape (such as that shown in FIG. 3) at a second end, and a gradually changing refractive index profile at regions of the preform between the first and second ends. As described above, such a preform can be drawn into optical fiber having a fiber dispersion that decreases along the fiber from one end thereof to the other.

In a similar manner, any of the disclosed refractive index profiles could be deposited at one end of the preform, and any of the remaining refractive index profiles could be deposited at the other end of the preform, the profile gradually changing from that at the one end to that at the remaining end.

The embodiments of FIGS. 6 and 8 could be formed by initially depositing a wedge-shaped coating on mandrel 60. The refractive index of the entire wedge-shaped coating would be that of core region 47 or 53. Thereafter coatings of uniform thickness would be formed. The thickness of the wedge-shaped coating would be such that, in the resultant fiber, the radius of the inner core region at one end of the fiber would be x μm larger than the radius at the other end of the fiber.

An example of a dispersion decreasing fiber that would require no variable thickness region, such as region 69, would be a fiber having the profile of FIG. 4(d) at one end and the profile of FIG. 3 at the other end. The radial positions of the outer core regions are the same. Only the shape of those outer regions changes. 

We claim:
 1. A method of making a glass article comprising the steps of:rotating a mandrel having a first and a second end, flowing, at a rate, a base glass reactant and a dopant glass reactant to a burner that produces a flame containing a stream of glass particles that is directed toward said mandrel, wherein the glass particles are deposited on said mandrel providing relative movement between said burner and said mandrel, so that said burner makes a traverse from the first end to the second end of said mandrel thereby depositing a first layer on said mandrel, making additional traverses of said burner from the first end to the second end of said mandrel to deposit additional layers on said first layer, the first layer and the additional layers having respective recipes which determine the composition of the layers, thereby forming a preform having layers and a refractive index profile, and, forming an optical fiber from said preform, wherein during the forming of a portion of the layers of said preform, the portion having a first layer, a last layer and intermediate layers therebetween, the rate of flowing of said dopant glass reactant varies in accordance with a first dopant reactant flow recipe as said burner traverses relative to said mandrel to deposit the first layer, the flow rate of said dopant glass reactant varies in accordance with a second dopant reactant flow recipe different from said first recipe as said burner traverses said mandrel to form a layer adjacent to said first layer, and each of the layers of the portion of the preform has an associated recipe which is different from the recipe of any other layer of the portion of the preform, and the varying of dopant glass reactant flow rate, during the deposition of said layers forming said preform, being such that said fiber has a first refractive index profile at a first end thereof and a second refractive index at a second end thereof opposite said first end, the first and second ends spaced apart by a length of fiber, and the refractive index profile changes from the first profile to the second profile over the length of said fiber between said ends, wherein the recipes are selected to cause the fiber group velocity dispersion to decrease along said fiber from said first end to said second end.
 2. The method of claim 1 wherein depositing of the preform layers occurs only while said burner makes a traverse from the first end to the second end of said mandrel.
 3. The method of claim 1 wherein, during the deposition of at least one preform layer which is not included within the portion of layers of said preform, the associated recipe of the at least one of said layers requires the flow rate of said dopant glass reactant to remain constant during the entire traverse of said burner along said mandrel.
 4. The method of claim 1 wherein said preform has a radius and a centerline and comprises a core region of layers located along the centerline of said preform, the core region having a radius less than the preform radius, and said portion of the layers of said preform are located in the core region.
 5. The method of claim 1 wherein said dopant glass reactant is selected from the group consisting of germanium, boron, and phosphorus. 